CN103173698A - Dispersed precipitated phase strengthened austenitic stainless steel with high Cr and high Ni and thermal processing method - Google Patents
Dispersed precipitated phase strengthened austenitic stainless steel with high Cr and high Ni and thermal processing method Download PDFInfo
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Abstract
The invention relates to dispersed precipitated phase strengthened austenitic stainless steel with high Cr and high Ni and a thermal processing method. The stainless steel component comprises the components in percentage by weight as follows: 0.2-0.8% of Si, not greater than 2% of Mn, 20-28% of Cr, 16-25% of Ni, not greater than 3% of Mo, 0-1% of Ti, 0-1% of W, 0-1% of Zr, 0-1% of V and the balance of Fe. The method comprises the following steps of: weighing according to the component proportion, refining and moulding; thermally forging, wherein the thermal rolling process is that rolling in four gates at 1180-1230 DEG C with the final rolling temperature over 1030 DEG C, wherein deformation is not less than 40% every time, and quenching and cooling; insulating for 20min to 1 hour at 1120-1200 DEG C; immediately quenching; performing high temperature annealing treatment at 950-1050 DEG C, insulating for 1.5-4 hours, then, furnace cooling or air cooling to room temperature, and directly quenching and quickly cooling. According to the invention, MC phase is separated out in the high temperature deformation process by comprehensively adding Ti, W, V, Zr and C elements. After thermal forming, relative materials are separated out through fine dispersion. Dimension of a second precipitated phase is controlled by the cooling rate through controlling subsequent thermal deformation processing parameters and the thermal treatment system.
Description
Technical field
The present invention is applicable to the material under extreme service condition, especially the 4th generation supercritical water reaction heap structured material; Also be applicable to the ultra supercritical coal generating system design and R﹠D of material.The approach of a kind of effective optimization of the high-temperature behavior that can improve austenitic stainless steel material particularly is provided.
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Background technology
Along with the high speed development of world economy and industry, high performance material more and more plays important effect, and austenitic stainless steel is exactly one of material of being favored very much.But along with industrial expansion, stainless application is Challenge also.As the 4th generation reactor be that the nuclear power system of new generation of representative has the characteristics such as high temperature and high pressure, high radiation field and strong corrosive environment mostly, the key part materials such as involucrum have been proposed harsher over-all properties (mechanical behavior under high temperature (as creep resisting ability), chemical property (as corrosion resistance) and Radiation hardness) requirement.Therefore in this field, the raising nuclear industry becomes problem demanding prompt solution with the over-all properties of material.
Summary of the invention
In order to address the above problem, the objective of the invention is a kind of microalloy Composition Design, be easy to form the microalloy element of disperse educt phase by interpolation, can be before Cr and C reaction, preferential and the C formation carbide that reacts, can avoid like this poor Cr phenomenon that causes because of Cr and C reaction, thus greatly improve material the anti intercrystalline corrosion performance the disperse educt high Ni austenitic stainless steel of high Cr and the thermal processing method strengthened mutually.
Technical scheme of the present invention is: the high Ni austenitic stainless steel of the high Cr that disperse educt is strengthened mutually, and the composition system of this austenitic stainless steel is not more than 0.2 for (wt.%): C; Si:0.2-0.8; Mn:0-2; Cr:20-28; Ni:16-25; Mo:0-3; Ti:0-1; W:0-1; Zr:0-1; V； 0-1; P is not more than 0.03; S is not more than 0.02; Surplus is Fe.
Further, the high Ni austenitic stainless steel of the high Cr that disperse educt is strengthened mutually, the composition system of this austenitic stainless steel is not more than 0.1 for (wt.%): C; Si:0.4-0.8; Mn:0-1.6; Cr:22-26; Ni:16-22; Mo:0-3; Ti:0.15-0.5; W:0-0.5; Zr:0.15-0.5; V； 0.15-0.5; P is not more than 0.02; S is not more than 0.015; Surplus is Fe.
Another purpose of the present invention is to provide above-mentioned stainless thermal processing method, and the present invention is by Composition Design, and take the industrial alloy piece as raw material, then moldings formed therefrom after melting in vacuum induction furnace carries out the high temperature hot-roll forming through after high temperature forging.
Specifically comprise with step:
Step 1. raw material: according to the mentioned component ratio, be respectively technically pure iron, the nickel plate; the chromium piece, silico briquette, manganese piece; vanadium iron, titanium sponge, zirconium sponge; tungsten; carbon-point and molybdenum bar, heating up at vacuum induction melting furnace (model 2G-0.025, frequency is 2500Hz) in vacuum melting vacuumizes; in the argon gas atmosphere protection, after all dissolving, alloy block carries out refining, mold:
Step 2. thermal distortion processing treatment:
At first, forging process is: initial forging temperature is 1160-1180 ℃, and final forging temperature is 900 ℃, and forging ratio is 3:1 approximately, then air cooling;
Secondly, the hot rolling technology significant parameter is: 1180-1230 ℃, finishing temperature is more than 1030 ℃, and four-pass rolls into, and each deflection is not less than 40%, rolls rear direct hardening cooling;
Step 3. thermal treatment: the alloy that above-mentioned steps was processed carries out solution treatment, and temperature is 1120-1200 ℃, insulation 20min-1h; Then hardening immediately; Carry out subsequently the high temperature anneal, temperature range 950-1050 ℃, insulation 1.5-4h, then or air cooling cold with stove be to room temperature, in order to control the size of precipitated phase, also can adopt accelerate cooling.To obtain how equally distributed multiple disperse educt phase.
Add heat resistance and the anti-void swelling performance that useful micro alloying element Ti, W, V and Zr improves austenitic stainless steel in the present invention in the SUS310 austenitic stainless steel.The generation of precipitated phase, size, distribution etc. all exert an influence to the performance of material, and can control the size of grain fineness number in austenitic stainless steel, so should both guarantee in the processing treatment process can this useful second-phase separate out, rationally control again size and the distribution of precipitated phase, bring into play the beneficial effect that it improves performance.
The performance that austenitic stainless steel has much room for improvement in nuclear reactor system mainly contains and shows as under the neutron irradiation of median dose, and its void swelling coefficient is larger.Studies show that super austenitic is stainless, it is the effective trap that absorbs the point defect that irradiation causes that disperse is distributed in second-phase in matrix and the phase interface between austenitic matrix, can greatly improve the anti-void swelling performance of material.By the microalloy Composition Design, be easy to form the microalloy element of disperse educt phase by interpolation, can be before Cr and C reaction, the preferential and C formation carbide that reacts, can avoid like this poor Cr phenomenon that causes because of Cr and C reaction, thereby greatly improve the anti intercrystalline corrosion performance of material.On the other hand, the fusing point of these MC is higher, and the precipitated phase of small and dispersed is also very useful to the mechanical property that improves material.In order to improve the deficiency of existing austenitic stainless steel, better bring into play its performance advantage, we by the interpolation microalloy element, and coordinate rational heat processing technique to improve the high-temperature behavior of austenitic steel on the basis of SUS310 austenitic stainless steel.
The invention has the beneficial effects as follows: SUS310 is austenitic stainless steel interalloy content and the comparatively excellent stable austenite stainless steel of performance, improves the existing shortcoming of its aspect of performance by adding trace alloying element on its basis.The element that comprehensive interpolation Ti, W, V and Zr and C element reaction ability are stronger, can separate out the MC phase in the high temperature deformation process, after thermoforming, the performance of relative material is more favourable (improves the intergranular corrosion that produces because of the poor Cr of crystal boundary because small and dispersed is separated out, hot strength, the anti-void swelling performance of improvement that the disperse of precipitated phase distributes and improves this austenitic stainless steel), so pass through in the present invention to control follow-up thermal distortion machined parameters and heat treating regime, and rate of cooling (directly hardening) is controlled the size of disperse second-phase.
Description of drawings
Fig. 1 is the displaing micro tissue topography of the example 3 immortal steel of austenite of the present invention and the distribution schematic diagram of disperse phase.
Fig. 2 is the displaing micro tissue topography of the example 4 immortal steel of austenite of the present invention and the distribution schematic diagram of disperse phase.
Embodiment
Below in conjunction with specific embodiment, technical scheme of the present invention is described further.
Embodiment 1:Contain Mn and Ti, W, V and Zr austenitic steel
The composition system of design is: Fe-22Cr-21Ni+0.6Ti+0.6Zr+0.5W+0.5V+1.5Mn+0.8Si+0.10C(wt. %).Raw material is the commodity gold that isozygoty, and smelts according to the method described above casting.Then be forged into rectangular parallelepiped and be convenient to processing and test use in high temperature 950-1200 ℃ scope.Adopt the forging ratio of 3:1, after forging is completed, specimen size is: 200mm * 140mm * 30mm.Then the forged steel sample is carried out high temperature rolling, 1190 ℃ of start rolling temperatures, finishing temperature is more than 1030 ℃, and four-pass rolls into, and the hot rolling total reduction is 80%, rolls rear direct hardening cooling fast.The sample of thermal distortion processing is incubated 50min 1150 ℃ of solution treatment; Then hardening immediately; Carry out subsequently the high temperature anneal, 1050 ℃ of temperature, insulation 3h, then or air cooling cold with stove is to room temperature.The intensity of comparing the gained sample with commercial steel is improved significantly, and its room temperature tensile strength is 615 MPa, yield strength 405 MPa, unit elongation 26.6%.
Embodiment 2: the austenitic steel that contains Mo and Ti, W, V and Zr
The composition system of design is: Fe-28Cr-18Ni+0.4Ti+0.4Zr+0.3Mo+0.3V+0.5Si+0.08C(wt.%).Raw material and melting method and aforesaid method are similar.Initial forging temperature is a little more than embodiment 1, and after forging is completed, specimen size is: 200mm * 140mm * 30mm.Then the forged steel sample is carried out high temperature rolling, 1200 ℃ of start rolling temperatures, finishing temperature is more than 1030 ℃, and four-pass rolls into, and the hot rolling total reduction is 80%, rolls rear direct hardening cooling fast.The sample of thermal distortion processing is incubated 40min 1180 ℃ of solution treatment; Then hardening immediately; Carry out subsequently the high temperature anneal, 1050 ℃ of temperature, insulation 3.5 h, then or air cooling cold with stove is to room temperature.The intensity of comparing the gained sample with commercial steel is improved significantly, and its room temperature tensile strength is 765 MPa, yield strength 525 MPa, unit elongation 33.6%.
Embodiment 3: contain Mn and small amount Ti, W, V and Zr austenitic steel
Raw material and fusion process are as mentioned above.The composition system of design is: Fe-25Cr-20Ni+0.2Ti+0.2Zr+0.1W+0.15V+1.2Mn+0.6Si+0.1C(wt. %).In above-mentioned steel ingot and get approximately 1/3, forge.The initial temperature of forging is 1180 ℃, and final temperature is 900 ℃, forging ratio 3:1.After forging is completed, specimen size is: 200mm * 140mm * 35mm.Then the forged steel sample is carried out high temperature rolling, 1200 ℃ of start rolling temperatures, finishing temperature is more than 1030 ℃, and four-pass rolls into, and the hot rolling total reduction is 80%, rolls rear direct hardening cooling fast.The sample of thermal distortion processing is incubated 60min 1160 ℃ of solution treatment; Then hardening immediately; Carry out subsequently the high temperature anneal, 1050 ℃ of temperature, insulation 3.5 h, then or air cooling cold with stove is to room temperature.Its microstructure is as shown in Fig. 1 (a), and the second-phase that as seen has disperse to distribute is distributed in matrix.Its room temperature tensile strength is 629.07 MPa, yield strength 429.11 MPa, and unit elongation 29.35%, the high temperature tensile strength under its 700 ℃ reaches 360 MPa, yield strength 295 MPa, unit elongation 33%.
Embodiment 4: the austenitic steel that contains Mo and a small amount of Ti, W, V and Zr
The composition system of the design of this austenitic stainless steel is: Fe-25Cr-20Ni+0.2Ti+0.2Zr+0.2W+0.15V+0Mn+2Mo+0.6Si+0.05C(wt.%).In above-mentioned steel ingot and get approximately 1/3, forge.The initial temperature of forging is 1160 ℃, and final temperature is 900 ℃, forging ratio 3:1.After forging is completed, specimen size is: 200mm * 140mm * 32mm.Then the sample after forging carries out hot rolling.The hot rolling technology significant parameter is: 1180 ℃ of start rolling temperatures, and four-pass rolls into, and each deflection is not less than 40%, rolls the direct hardening of rear sample cooling, and the sample of thermal distortion processing is incubated 50min 1180 ℃ of solution treatment; Then hardening immediately; Carry out subsequently the high temperature anneal, 1050 ℃ of temperature, insulation 3 h, then or air cooling cold with stove is to room temperature.Its microstructure is as shown in Fig. 1 (b), and the second-phase that as seen has disperse to distribute is distributed in matrix.Its room temperature tensile strength is 835 MPa, yield strength 645 MPa, and unit elongation 43.25%, the high temperature tensile strength under its 700 ℃ reaches 445 MPa, yield strength 385 MPa, unit elongation 28.5%.
Claims (3)
1. disperse educt is strengthened the high Ni austenitic stainless steel of high Cr mutually, it is characterized in that, the composition system of this austenitic stainless steel is that wt.%:C is not more than 0.2; Si:0.2-0.8; Mn:0-2; Cr:20-28; Ni:16-25; Mo:0-3; Ti:0-1; W:0-1; Zr:0-1; V； 0-1; P is not more than 0.03; S is not more than 0.02; Surplus is Fe.
2. disperse educt is strengthened the high Ni austenitic stainless steel of high Cr mutually, it is characterized in that, the composition system of this austenitic stainless steel is that wt.%:C is not more than 0.1; Si:0.4-0.8; Mn:0-1.6; Cr:22-26; Ni:16-22; Mo:0-3; Ti:0.15-0.5; W:0-0.5; Zr:0.15-0.5; V； 0.15-0.5; P is not more than 0.02; S is not more than 0.015; Surplus is Fe.
3. a stainless thermal processing method as described in right 1 or 2, is characterized in that, specifically comprises with step:
Step 1. raw material: according to the mass percent of above-mentioned each composition, respectively with technically pure iron, the nickel plate; the chromium piece, silico briquette, manganese piece; vanadium iron; titanium sponge, zirconium sponge, tungsten; carbon-point and molybdenum bar take according to quantity; be placed in the vacuum induction melting furnace intensification and vacuumize, in the argon gas atmosphere protection, carry out refining, mold after alloy block all dissolves:
Step 2. thermal distortion processing treatment:
At first, forging process is: initial forging temperature is 1160-1180 ℃, and final forging temperature is 900 ℃, and forging ratio is 3:1 approximately, then air cooling;
Secondly, the hot rolling technology significant parameter is: 1180-1230 ℃, finishing temperature is more than 1030 ℃, and four-pass rolls into, and each deflection is not less than 40%, rolls rear direct hardening cooling;
At last, thermal treatment: the alloy that above-mentioned steps was processed carries out solution treatment, and temperature is 1120-1200 ℃, insulation 20min-1h; Then hardening immediately; Carry out subsequently the high temperature anneal, temperature range 950-1050 ℃, insulation 1.5-4h, then or air cooling cold with stove is to room temperature.
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103526103A (en) * | 2013-09-27 | 2014-01-22 | 泰州永兴合金材料科技有限公司 | Smelting method of garnierite type lateritic nickel ore and product of garnierite type lateritic nickel ore |
| CN104651589A (en) * | 2015-02-05 | 2015-05-27 | 北京科技大学 | Process for hot deformation of fine 316LN austenite stainless steel grains |
| CN105154793A (en) * | 2015-09-25 | 2015-12-16 | 安阳工学院 | High-strength high-corrosion-resistance double-phase heat resistant steel |
| CN106609336A (en) * | 2015-10-26 | 2017-05-03 | 威尔机械江苏有限公司 | Acid-resistant stainless steel and production method thereof |
| CN107217215A (en) * | 2017-05-26 | 2017-09-29 | 黄曦雨 | Austenitic stainless steel and its application and bead-welding technology |
| CN108950404A (en) * | 2018-08-13 | 2018-12-07 | 广东省材料与加工研究所 | A kind of austenitic heat-resistance steel and preparation method thereof containing zirconium |
| CN108977718A (en) * | 2018-07-25 | 2018-12-11 | 江苏永达电源股份有限公司 | A kind of alloy that creep-resistant property is promoted |
| CN109570508A (en) * | 2018-12-13 | 2019-04-05 | 北京科技大学 | The preparation method of the oxide dispersion strengthening ferrite steel of double grain size distributions |
| CN112662932A (en) * | 2019-10-15 | 2021-04-16 | 中国石油化工股份有限公司 | TWIP steel and preparation method thereof |
| CN112981068A (en) * | 2021-02-02 | 2021-06-18 | 北京科技大学 | Method for improving toughness of microalloyed ledge steel casting by utilizing deformation induced precipitation |
| CN113061802A (en) * | 2021-02-07 | 2021-07-02 | 中国科学院金属研究所 | High-strength austenitic aged stainless steel resistant to corrosion of concentrated nitric acid containing oxidative ions and preparation method thereof |
| CN114807741A (en) * | 2021-09-02 | 2022-07-29 | 中国科学院金属研究所 | Method for improving performance of austenitic stainless steel based on carbide precipitation |
| CN115976417A (en) * | 2023-02-17 | 2023-04-18 | 东北大学 | High-nitrogen low-molybdenum super austenitic stainless steel and preparation method thereof |
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Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103526103A (en) * | 2013-09-27 | 2014-01-22 | 泰州永兴合金材料科技有限公司 | Smelting method of garnierite type lateritic nickel ore and product of garnierite type lateritic nickel ore |
| CN104651589A (en) * | 2015-02-05 | 2015-05-27 | 北京科技大学 | Process for hot deformation of fine 316LN austenite stainless steel grains |
| CN105154793A (en) * | 2015-09-25 | 2015-12-16 | 安阳工学院 | High-strength high-corrosion-resistance double-phase heat resistant steel |
| CN106609336A (en) * | 2015-10-26 | 2017-05-03 | 威尔机械江苏有限公司 | Acid-resistant stainless steel and production method thereof |
| CN107217215A (en) * | 2017-05-26 | 2017-09-29 | 黄曦雨 | Austenitic stainless steel and its application and bead-welding technology |
| CN108977718A (en) * | 2018-07-25 | 2018-12-11 | 江苏永达电源股份有限公司 | A kind of alloy that creep-resistant property is promoted |
| CN108950404A (en) * | 2018-08-13 | 2018-12-07 | 广东省材料与加工研究所 | A kind of austenitic heat-resistance steel and preparation method thereof containing zirconium |
| CN109570508B (en) * | 2018-12-13 | 2022-03-29 | 北京科技大学 | Preparation method of oxide dispersion strengthened ferrite steel with double-grain size distribution |
| CN109570508A (en) * | 2018-12-13 | 2019-04-05 | 北京科技大学 | The preparation method of the oxide dispersion strengthening ferrite steel of double grain size distributions |
| CN112662932A (en) * | 2019-10-15 | 2021-04-16 | 中国石油化工股份有限公司 | TWIP steel and preparation method thereof |
| CN112981068A (en) * | 2021-02-02 | 2021-06-18 | 北京科技大学 | Method for improving toughness of microalloyed ledge steel casting by utilizing deformation induced precipitation |
| CN113061802A (en) * | 2021-02-07 | 2021-07-02 | 中国科学院金属研究所 | High-strength austenitic aged stainless steel resistant to corrosion of concentrated nitric acid containing oxidative ions and preparation method thereof |
| CN113061802B (en) * | 2021-02-07 | 2022-05-31 | 中国科学院金属研究所 | High-strength austenitic aged stainless steel resistant to corrosion of concentrated nitric acid containing oxidative ions and preparation method thereof |
| CN114807741A (en) * | 2021-09-02 | 2022-07-29 | 中国科学院金属研究所 | Method for improving performance of austenitic stainless steel based on carbide precipitation |
| CN114807741B (en) * | 2021-09-02 | 2023-09-22 | 中国科学院金属研究所 | Method for improving austenitic stainless steel performance based on carbide precipitation |
| CN115976417A (en) * | 2023-02-17 | 2023-04-18 | 东北大学 | High-nitrogen low-molybdenum super austenitic stainless steel and preparation method thereof |
| CN115976417B (en) * | 2023-02-17 | 2024-04-19 | 东北大学 | High-nitrogen low-molybdenum super austenitic stainless steel and preparation method thereof |
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